Patent Application
20150294774
This application claims priority to European patent application serial number 14164576.0 filed on Apr. 14, 2014 and incorporated herewith by reference in its entirety.
The invention refers to ferrous metallurgy and can be used while producing grain-oriented electrical steel deployed in a manufacture of power transformer cores.
Subject to a purpose of transformers, grain-oriented steel is subdivided into steel having restricted (B8<1.85 T), elevated (B8=1.86-1.89 T) and high (B8=1.90-1.95 T) permeability (B8—Induction-magnetic flux density, tesla; 8—Intensity of a field, a/cm). The first group is employed for producing distribution transformers. The second one—partially for distribution transformers and partially for power ones, and the third group is mainly used in power distribution industry. A share of the third group metal is estimated as 35-45% with a possible upcoming increase up to 45-50%.
Steel's magnetic properties and, in particular, induction B8, is considerably defined by a degree of sophistication of the Goss texture ({110}<001>) formed during the secondary recrystallization ({110}<001>—texture, {110}—plane, <001>—direction, relatively direction of deformation). The first group metal is characterized by the average deviation of Goss grains from the perfect orientation by of 7-8 deg., the second group—by a 4-6 degree deviation and the third group—by a 3-4 degree deviation.
Formation of the prefect texture requires compliance with the following basic conditions:
Formation in the primary recrystallization matrix of the texture expressed by the octahedral component ({111}<112>) (absorbed component) and sharp Goss grains (absorbing component), whose intensity is restricted;
Steel with restricted permeability, whose share for the last decade has dropped from 65 to 20%, is produced under the sulfide inhibiting method with the double cold rolling and recrystallization annealing in an intermediate thickness [1].
Steel of elevated permeability is also produced under a double cold rolling technique. An option of Kawasaki Company (at present, JFE) provides for an improvement of properties due to sharpening of Goss component in the subsurface area of hot-rolled coils [2], which is then reproduced in the finished material under the texture inheritance mechanism [3]. However, due to insufficient intensity of the octahedral texture the magnetic induction B8 is limited by 1.86-1.89 T. Much the same induction level B8 is typical of nitride inhibited steel [4] practiced in Russia, China and Eastern Europe countries, with the technology being characterized by a sufficient intensity of the absorbed texture. In the meantime, a more dispersed Goss component of the hot-rolled material texture prevents from increasing B8 up to 1.90 T and more.
Currently, high permeability steel is produced under two production routes developed by Nippon Steel. The general condition for these technologies is a single cold rolling with a high deformation thus providing for both an expansion of the octahedral component and sharpening of the Goss component. The difference of these routes is a method of managing impurity systems. The first classical technology [5,6] practiced from the beginning of 1970s provides for a formation of the required impurity system during hot rolling, but the second one introduced in the middle of 1990s [7,8] is based on feeding the key modifying element, i.e. nitrogen during chemical and heat processing in the final thickness.
The basic disadvantage of the first route is a necessity of high-temperature slab heating accompanied by an abundant slag formation, whose removal is quite labor-intensive and requires additional material expenses.
First and foremost, the second route significantly restricts a throughput of decarburizing annealing furnaces, and, secondly, provides for usage of the environmentally unfriendly ammonia technology.
Disadvantages of both technologies include:
A challenge of the assumed invention is a development of a new technology of high permeability grain-oriented steel production free of the above-mentioned drawbacks, which is based on a combination of merits of technological routes practiced by the Japanese company Kawasaki (JFE) and Russian company NLMK.
The invention refers to ferrous metallurgy, in particular, to production of grain-oriented electrical steel deployed in a manufacture of power transformer cores. Ensuring high magnetic permeability of steel and homogeneity of the magnetic properties requires slab casting, slab heating, rough and finishing hot rolling, cooling, pickling, double cold rolling with an intermediary decarburizing annealing, MgO coating application, box annealing and flattening annealing distinctive in that the steelmaking is implemented at the following ratio of the components, % wt: C=0.018-0.035; Mn=0.15-0.40; Si=3.15-3.50; Al=0.010-0.035; N2=0.0090.015; Cu=0.4-0.6 with the balance of Fe and unavoidable impurities, at the carbon-silicon concentration chosen so that during the finishing hot rolling within the range of 1130-1280° C. the austenite ratio comes to 2-10%, and with the rolling at the total deformation ratio of 80-95% and the rolling end temperature of 950-1030° C. After rolling strips are cooled within the time not exceeding two seconds, but the heating for the high-temperature annealing in the temperature range of 400-700° C. is carried out at the rate of 20-25° C./hour.
The technical result of the invention is to ensure high magnetic permeability of steel.
To achieve the above-stated technical result the production process for high permeability grain-oriented electrical steel, which includes steelmaking, slab casting, slab heating, rough and finishing hot rolling, cooling, pickling, double cold rolling with intermediary decarburizing annealing, MgO coating application, box annealing and flattening annealing comprises steelmaking at the following mixture ratio, % wt: C 0.018-0.035, Mn 0.10-0.40, Si 3.0-3.50, Al 0.01-0.035, N2 0.008-0.015, Cu 0.4-0.6, with the balance of Fe and unavoidable impurities, at carbon-silicon ratio chosen so that the austenite fraction during the finishing hot rolling within the range of 1150-1050° C. comes to 2-10%, at that, before the finishing cold rolling the breakdown bar temperature is maintained in the range of 1130-1280° C. (preferably 1180-1240° C.) and the rolling is carried out at an overall deformation ratio of 80-95% and the rolling end temperature of 950-1030° C. (preferably 970-1030° C.). After rolling the strips are subject to cooling within time not exceeding two seconds, but heating for the high-temperature annealing is carried out within the temperature range of 400-700° C. at the rate of 15-30° C./hour (preferably 20-25° C./hour). Reaching the required temperature before the finishing rolling requires either breakdown bars being heated in open-flame or induction furnaces or being cast in compact strip production lines.
The above-mentioned technology conceptually differs from the operating ones in terms of reaching high permeability under a double cold rolling technique. Efficiency of the proposed technology is a remarkable decrease of expenses per production stage along with an exclusion of time-consuming and environmentally unfriendly operations (high-temperature slab heating, nitriding and others) from the processing cycle.
Differences between acknowledged [5-8] and proposed technologies of high permeability steel production arise from scheme comparison in
Maintaining the structure and texture of hot-rolled coils typical of the deformed condition (at minimal recrystallization development), at which the subsurface layer ( 1/10- 1/7 over thickness) is noted for a formation of the sharp Goss textured area obtained by:
Temperature rise for the rolling end is possible by means of:
Decrease of the phase recrystallization is obtained as a result of the rational choice of the carbon-silicon concentration ratio.
A conspicuous octahedral texture in the primary recrystallization matrix is obtained as a result of:
Nitrogen and copper precipitating from the supersaturated solution at the polygonization stage contribute to increasing the primary recrystallization temperature and provide for more than double strengthening of the octahedral component in the primary recrystallization matrix.
Thus, the assumed technology includes the following operations as the key ones:
Steelmaking with the following chemical composition, % wt: C (0.018-0.035), Mn (0.1-0.4), Si (3.0-3.5), Al (0.01-0.03), N2 (0.08-0.015), Cu (0.4-0.6) with the balance of Fe and unavoidable impurities. Steel was poured in the continuous casting machines to obtain slabs of 220 mm thick. Slabs were heated in push furnaces and rolled in the rough mill to breakdown bars of 30-40 mm thick. Temperature of the rolling end came to 1200-1220° C.
Breakdown bars were heated in a tunnel open-flame furnace. After descale sprays the temperature of breakdown bars came to 1210-1240° C. with a subsequent finishing rolling to the strip of 2.5 mm thick.
The temperature of the finishing rolling end was changed in the range of 930-1030° C. by changing the deformation speed and thickness of the intermediate breakdown bars. Subsequent stages included pickling, first cold rolling for 0.65 mm, decarburizing annealing, second cold rolling for 0.30 mm, MgO coating application, box annealing with the speed limit for coil heating within the range of 400-700° C. up to 15-30° C./hour, flattening annealing with an application of the insulation coating. Table 1 contains data defining an influence of the hot rolling termination temperature on steel's magnetic properties.
These data mean that an increase of the rolling temperature permits reaching a level of the magnetic properties typical of high permeability steel, which is explained by suppression of the recrystallization processes at a hot deformation by means of both softening under the dynamic recovery mechanism and as a result of restraining the phase recrystallization defined by the efficient ratio of the ferrite-promoting [Si] and austenite-promoting [C] elements.
Steelmaking with the following chemical composition, % wt: C (0.025-0.041), Mn (0.15-0.25), Si (3.15-3.17), Al (0.016-0.018), N2 (0.009-0.011), Cu (0.4-0.6), with the balance of Fe and unavoidable impurities. Steel was poured in the continuous casting machines to obtain slabs of 220 mm thick.
Slabs were heated in walking-beam furnace and rolled in the rough mill to breakdown bars of 50 mm thick. The rolling end temperature came to 1210-1230° C.
Breakdown bars were heated in an open-flame furnace up to 1230-1250° C. After descale sprays the temperature of breakdown bars came to 1180-1200° C. Breakdown bars were deformed in the finishing train to strips of 2.2 mm thick. The rolling end temperature was maintained in the range of 990-1010° C.
The subsequent metal processing corresponded to that one described in the Example 1. Intermediate thickness was 0.60 mm, final one-0.30 mm. Table 2 shows the results obtained.
Data of the Table 2 imply the following:
While the invention has been described with reference to an exemplary embodiment, it will be understood by those skilled in the art that various changes may be made and equivalents may be substituted for elements thereof without departing from the scope of the invention. In addition, many modifications may be made to adapt a particular situation or material to the teachings of the invention without departing from the essential scope thereof. Therefore, it is intended that the invention not be limited to the particular embodiment disclosed as the best mode contemplated for carrying out this invention, but that the invention will include all embodiments falling within the scope of the appended claims.
| Number | Date | Country | Kind |
|---|---|---|---|
| 14164576.2 | Apr 2014 | EP | regional |
